Intense visible photoluminescence in Ba„Zr0.25Ti0.75
Transcrição
Intense visible photoluminescence in Ba„Zr0.25Ti0.75
APPLIED PHYSICS LETTERS 90, 011901 共2007兲 Intense visible photoluminescence in Ba„Zr0.25Ti0.75…O3 thin films L. S. Cavalcantea兲 and M. F. C. Gurgel Laboratório Interdisciplinar de Eletroquímica e Cerâmica, Departamento de Química, Universidade Federal de São Carlos, P.O. Box 676, 13565-905 São Carlos, São Paulo, Brazil A. Z. Simões, E. Longo, and J. A. Varela Laboratório Interdisciplinar em Cerâmica, Departamento de Físico-Química, Instituto de Química, Universidade Estadual Paulista, P.O. Box 355, 14801-907 Araraquara, São Paulo, Brazil M. R. Joya and P. S. Pizani Departamento de Física, Universidade Federal de São Carlos, P.O. Box 676, 13565-905 São Carlos, São Paulo, Brazil 共Received 1 September 2006; accepted 25 November 2006; published online 2 January 2007兲 Photoluminescence at room temperature in Ba共Zr0.25Ti0.75兲O3 thin films was explained by the degree of structural order-disorder. Ultraviolet-visible absorption spectroscopy, photoluminescence, and first principles quantum mechanical measurements were performed. The film annealed at 400 ° C for 4 h presents intense visible photoluminescence behavior at room temperature. The increase of temperature and annealing time creates 关ZrO6兴 – 关TiO6兴 clusters in the lattice leading to the trapping of electrons and holes. Thus, 关ZrO5兴 – 关TiO6兴 / 关ZrO6兴 – 关TiO6兴 clusters were the main reason for the photoluminescence behavior. © 2007 American Institute of Physics. 关DOI: 10.1063/1.2425013兴 Photoluminescence 共PL兲 is a powerful tool to discover the energy levels of materials when used in combination with absorption and PL excitation measurements. PL provides fundamental information of the structural degree within the band gap of materials. Much interest has been focused on the photoluminescence of disordered or nanostructured material, since this phenomenon was first observed in porous silicon at room temperature.1 In this context, the development of new environmentally friendly materials is of fundamental importance. ABO3 perovskites 共A = Ba, Ca, Sr and B = Ti兲 have been the focus of research aiming at their potential for photoluminescence properties.2–5 Kan et al.6 reported that the main cause for PL emission at room temperature in polycrystalline SrTiO3 is oxygen deficiency. However, there are several papers explaining the favorable conditions for PL emission in materials presenting an order-disorder degree.7–9 Recently, Ba共ZrxTi1−x兲O3 共BZT兲 has been chosen as an alternative material to 共Ba, Sr兲TiO3 in the fabrication of ceramic or thin films because the Zr4+ ion is chemically more stable than the Ti4+ ion.10,11 However, its PL properties have not yet been reported. In this letter, we present the role of order-disorder to explain the intense visible photoluminescence of Ba共Zr0.25Ti0.75兲O3 共BZT兲 thin films at room temperature. The films annealed at 400 ° C for different times and at 700 ° C for 2 h were characterized by ultraviolet-visible 共UV-vis兲 absorption spectroscopy, PL, and quantum mechanical calculation measurements. This dual approach renders a plausible quantitative description of BZT thin film behavior under laser excitation and an interesting correlation with experimental results. Quantum mechanical calculations have been carried out with the CRYSTAL98 package,12 which is based on both density functional and Hartree-Fock methods. The gradient-corrected correlation functional by Lee et al.13 and Becke14 was used, combined with the Becke3 exchange functional, B3LYP. The atomic centers have been described a兲 Electronic mail: [email protected] by all electron basis sets 9763-311共d631兲G for Ba,15 976 -31共d62兲G* for Zr,15 86-411共d31兲G for Ti,16 and 6-31G* for O.16 BZT thin films were prepared by the soft chemical method, as described in the following article.17 The viscosity of the resulting solution was adjusted to 13 mPa s, controlling the water content using a Brookfield viscosimeter. The polymeric solution was spin coated on the substrates by a commercial spinner operating at 7500 rpm for 20 s 共spin coater KW-4B, Chemat Technology兲. Such solution was deposited onto the Pt/ Ti/ SiO2 / Si substrates via a syringe filter to avoid particulate contamination. After deposition, the films were kept on a hot plate at 150 ° C in air ambient for 10 min to remove residual solvents. The films were annealed at 400 ° C for 1, 2, 4, 8, and 16 h and at 700 ° C for 2 h with a heating rate of 3 ° C / min in oxygen atmosphere. The UV-vis absorption spectra of the optical absorbance for disordered BZT thin films and crystalline BZT film were taken at room temperature using Cary 5G equipment. The PL spectra of the thin films were taken with a U-1000 JobinYvon double monochromator coupled to a cooled GaAs photomultiplier and a conventional photon counting system. The 514.5 nm exciting wavelength of an argon ion laser was used, with the laser’s maximum output power kept at 30 mW. A cylindrical lens was used to prevent the sample from overheating. The slit width used was 100 m. All measurements were taken at room temperature. Figure 1 illustrates the UV-vis spectral dependence of absorbance for BZT thin films annealed at 400 ° C for different times and annealed at 700 ° C for 2 h in oxygen atmosphere. The optical band values obtained from the UV-vis spectroscopy is shown in Fig. 1. The exponential optical absorption edge and the optical band gap are controlled by the structural order-disorder degree in the BZT film lattice. The increase of band gap can be ascribed to the reduction of defects or impurities that give rise to intermediary energy levels in the band gap region of disordered BZT films. The films annealed at 400 ° C for 1, 2, 0003-6951/2007/90共1兲/011901/3/$23.00 90, 011901-1 © 2007 American Institute of Physics Downloaded 12 Jan 2007 to 200.136.226.67. Redistribution subject to AIP license or copyright, see http://apl.aip.org/apl/copyright.jsp 011901-2 Appl. Phys. Lett. 90, 011901 共2007兲 Cavalcante et al. FIG. 1. UV-vis absorbance spectra for the BZT thin films annealed at 400 ° C for 共a兲 1 h, 共b兲 2 h, 共c兲 4 h, 共d兲 8 h, and 共e兲 16 h. Inset shows the BZT film annealed at 700 ° C for 共f兲 2 h in oxygen atmosphere. 4, 8, and 16 h showed a similar spectral dependence to that found in amorphous semiconductors such as silicon and insulators 关see Figs. 1共a兲–1共e兲兴, while the BZT film annealed at 700 ° C showed a typical band for crystalline materials. In addition, in the high energy region of the absorbance curve 关see Fig. 1共f兲兴, the optical band gap energy is related to the absorbance and to the photon energy by Wood and Tauc.18 In the disordered films, the absorbance measurements suggest a nonuniform band gap structure with a tail of localized states. The optical energy band gap is related to the absorbance and to the photon energy by Eq. 共1兲: 2 h␣ ⬀ 共h − Eopt g 兲 , 共1兲 where ␣ is the absorbance, h is the Planck constant, is the frequency, and Eopt g is the optical band gap. Table I illustrates the charge variations for each 关TiO6兴 and 关ZrO5兴, after displacement of Zr to deformation of Ba共Zr0.25Ti0.75兲O3, and the charge difference between the individual clusters of periodic models for theoretical gap energies. Theoretical calculations indicate that the atom generated intermediary energy levels in the band gap, increasing the trapping of electrons and holes. The trapping of charges is the condition for a good PL emission. This accordance between experimental and theoretical gap energy results illustrates the reliability of our distorted model. Figure 2 illustrates the PL spectra recorded at room temperature for the BZT thin films annealed at 400 ° C for different times and annealed at 700 ° C for 2 h in oxygen atmo- FIG. 2. PL spectra of BZT thin films annealed at 400 ° C for 共a兲 1 h, 共b兲 2 h, 共c兲 4 h, 共d兲 8 h, and 共e兲 16 h and 共f兲 annealed at 700 ° C for 2 h in oxygen atmosphere. Inset shows experimental Eg共exp兲 and theoretical Eg共theo兲 gap energies for the films annealed at 400 ° C for different times. sphere. The excitation line of argon ion laser was 514.5 nm 共⬵2.41 eV兲. The PL emission is associated with the structural order-disorder degree. A broad intense luminescence in the visible region 共yellow兲 with a maximum at about 568 nm was observed. The emission band profile is a typical multiphonon process, i.e., a system in which the relaxation occurs by several paths, involving the participation of numerous levels within the perovskite band gap. The presence of several delocalized energy levels in the band gap and the structural disorder are responsible for the weak PL behavior observed in Figs. 2共a兲 and 2共b兲. The increase of annealing time reduces the oxygen vacancies and decrease the structural disorder, due to the presence of 关ZrO5兴 – 关TiO6兴 clusters leading to an increase of PL intensity 关Fig. 2共c兲兴. Fig. 2共d兲 and 共e兲 illustrates that the PL intensity reduces with the increase of annealing time due the formation of the 关关ZrO6兴 – 关TiO6兴 clusters as can be observed by the increase of optical gap 共see inset in Fig. 2兲. When the annealing temperature is increased, ordered 关ZrO6兴 – 关TiO6兴 clusters are obtained and the charge transference between them 关Figs. 1共f兲 and 2共f兲兴 is inhibited. Experimental and theoretical band gap results strongly indicate that PL is directly linked to the optical tail existing in the disordered films 共see inset in Fig. 2兲. Absorbance measurements associated with the PL properties of noncrystalline BZT thin films lead to a nonuniform band gap structure with a tail of delocalized levels and mobile edges. The nature of these exponential optical TABLE I. Charge variations for the 关TiO6兴, 关ZrO5兴, and 关TiO6兴 – 关ZrO5兴 clusters and experimental gap energy Eg共exp兲 in axis x 共Fig. 1兲 and theoretical gap energy Eg共theo兲 for Ba共Zr0.25Ti0.75兲O3 thin films. Displacement in axis z 共Å兲 Charge of the 关TiO6兴 共e−兲 Charge of the 关ZrO5兴 共e−兲 Charge difference 关TiO6兴 – 关ZrO5兴 共e−兲 Eg共exp兲 共eV兲 Eg共theo兲 共eV兲 0.75 0.70 0.50 0.40 0.20 0.00 −2.37 −2.35 −2.26 −2.20 −2.06 −1.93 −1.98 −1.97 −1.90 −1.85 −1.74 −1.60 −0.39 −0.38 −0.36 −0.35 −0.32 −0.33 2.20 2.27 2.53 2.65 2.93 3.78 2.23 2.32 2.50 2.62 2.94 3.70 Downloaded 12 Jan 2007 to 200.136.226.67. Redistribution subject to AIP license or copyright, see http://apl.aip.org/apl/copyright.jsp 011901-3 Appl. Phys. Lett. 90, 011901 共2007兲 Cavalcante et al. FIG. 3. Wide band model: 共a兲 before excitation, 共b兲 excitation→ formation of STE, and 共c兲 after excitation→ recombination of e− and h0. edges and tails is probably associated with defects promoted by the disordered structure. A wide band model of photoluminescence process in Ba共Zr0.25Ti0.75兲O3 thin films is shown in Fig. 3. The localized levels are energetically distributed being able to excite the trapped electrons 关see Fig. 3共a兲兴. According to the hypothesis of Korzhik et al.19 there are vacant localized states linked to local defects such as oxygen vacancies in the band gap above the valence band and below the conduction band.6 In the model of Leonelli and Brebner20 some electrons are promoted to the conduction band by absorption of photon, creating small polarons. The polarons interact with holes trapped in the crystal 共defects or impurities兲 and form selftrapped excitons 共STEs兲 that contribute to the visible PL emission 关see Fig. 3共b兲兴. The short and intermediate range structural defects generate localized states in the band gap and inhomogeneous charge distribution in the cell, thus allowing the trapping of electrons. Furthermore, it will also leave an electron hole that can flow as current exactly like a physical charged particle. Figure 3共c兲 describes the recombination process in which an electron of conduction band loses its energy and reoccupies the energy levels of an electron hole 共h0兲 in the valence band. This model suggests that the increase of annealing time reduces the surface, creating electron-captured oxygen’s vacancies, according to Eq. 共2兲: 1 共ZrO5 · Vzo兲 + O2 → ZrO2 , 2 共2兲 * z · ·· where VO = VO , VO , or VO . z 兲 cluster acts as hole traps, In the complex, 共ZrO5 · VO z while the VO vacancy tends to trap electrons 共z = · or ··兲 or holes 共z = *兲. Previous studies of our group assume the existence of TiO6 and distorted ZrO6 clusters in lattice before complete film crystallization. A random mixture of TiO6 and z 兲 complex octahedral linked by barium ions is 共ZrO5 · VO found in this case. The displacements performed in axis z for Zr atom, such as breaking of the bonds 共Zr–O兲 and formation z , give the band gap energy approaching experiof vacancy VO mental data. In BZT, the transport properties such as electri- cal conductivity and photoluminescence are governed by electrons, as well as some phenomena are related to holes. In conclusion, intense visible photoluminescence 共around 568 nm兲 was observed for the Ba共Zr0.25Ti0.75兲O3 thin films and is caused by structural defects such as 关ZrO5兴 – 关TiO6兴 clusters. The oxygen vacancies play an important role on the PL emission via a recombination of elecz 兲 with photoexcited holes in trons in oxygen vacancies 共VO the valence band. Our theoretical models are consistent with the experimental data and confirm that the localized levels in the band gap are controlled by the order-disorder degree in the lattice. The authors gratefully acknowledge the financial support of the Brazilian financing agencies CAPES, CNPq, and FAPESP. L. T. Canham, Appl. Phys. Lett. 57, 1046 共1990兲. F. M. Pontes, C. D. Pinheiro, E. Longo, E. R. Leite, S. R. de Lazaro, R. Magnani, P. S. Pizani, T. M. Boschi, and F. Lanciotti, Jr., J. Lumin. 104, 175 共2003兲. 3 F. M. Pontes, C. D. Pinheiro, E. Longo, E. R. Leite, S. R. de Lazaro, J. A. Varela, P. S. Pizani, T. M. Boschi, and F. Lanciotti, Jr., Mater. Chem. Phys. 78, 227 共2003兲. 4 F. M. Pontes, E. Longo, E. R. Leite, E. J. H. Lee, J. A. Varela, P. S. Pizani, C. E. M. Campos, F. Lanciotti, V. Mastellaro, and C. D. Pinheiro, Mater. Chem. Phys. 77, 598 共2003兲. 5 E. Longo, E. Orhan, F. M. Pontes, C. D. Pinheiro, E. R. Leite, J. A. Varela, P. S. Pizani, T. M. Boschi, F. Lanciotti, Jr., A. Beltràn, and J. Andrès, Phys. Rev. B 69, 125115 共2004兲. 6 D. Kan, T. Terashima, R. Kanda, A. Masuno, K. Tanaka, S. Chu, H. Kan, A. Ishizumi, Y. Kanemitsu, Y. Shimakawa, and M. Takano, Nat. Mater. 4, 816 共2005兲. 7 I. A. Souza, A. Z. Simões, E. Longo, J. A. Varela, and P. S. Pizani, Appl. Phys. Lett. 88, 211911 共2006兲. 8 E. Orhan, F. M. Pontes, M. A. Santos, E. R. Leite, A. Beltrán, J. Andrés, T. M. Boschi, P. S. Pizani, J. A. Varela, C. A. Taft, and E. Longo, J. Phys. Chem. B 108, 9221 共2004兲. 9 E. R. Leite, L. P. S. Santos, N. L. V. Carreño, E. Longo, C. A. Paskocimas, J. A. Varela, F. Lanciotti, Jr., C. E. M. Campos, and P. S. Pizani, Appl. Phys. Lett. 78, 2148 共2001兲. 10 Z. Yu, C. Ang, R. Guo, and A. S. Bhalla, Appl. Phys. Lett. 81, 1285 共2002兲. 11 A. Dixit, S. B. Majumder, R. S. Katiyar, and A. S. Bhalla, Appl. Phys. Lett. 82, 2679 共2003兲. 12 V. R. Saunders, R. Dosevi, C. Roetti, M. Causa, N. M. Harrison, and C. M. Zicovich-Wilson, CRYSTAL98 User’s Manual 共University of Torino, Torino, 1998兲. 13 C. Lee, W. Yang, and R. G. Parr, Phys. Rev. B 37, 785 共1988兲. 14 A. D. Becke, J. Chem. Phys. 98, 5648 共1993兲. 15 http://www.tcm.phy.cam.ac.uk/~mdt26/crystal.html 16 http://www.crystal.unito.it/Basis_Sets/Ptable.html 17 F. M. Pontes, M. T. Escote, C. C. Escudeiro, E. R. Leite, E. Longo, A. J. Chiquito, P. S. Pizani, and J. A. Varela, J. Appl. Phys. 96, 4386 共2004兲. 18 D. L. Wood and J. Tauc, Phys. Rev. B 5, 3144 共1972兲. 19 M. V. Korzhik, V. B. Pavlenko, T. N. Timoschenko, V. A. Katchanov, A. V. Singovskii, A. N. Annenkov, V. A. Ligum, I. M. Solskii, and J. P. Peigneux, Phys. Status Solidi A 154, 779 共1996兲. 20 R. Leonelli and J. L. Brebner, Phys. Rev. B 33, 8649 共1986兲. 1 2 Downloaded 12 Jan 2007 to 200.136.226.67. Redistribution subject to AIP license or copyright, see http://apl.aip.org/apl/copyright.jsp
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